PHYSICAL REVIEW B VOLUME 60, NUMBER 6 1 AUGUST 1999-II Structure and physical properties of the quaternary Remeika-phase compound Yb 5 Pt 6 In 16 Bi 2 E. G. Moshopoulou, M. F. Hundley, R. Movshovich, J. D. Thompson, J. L. Sarrao, * and Z. Fisk * Los Alamos National Laboratory, Los Alamos, New Mexico 87545 E. Felder, M. Chernikov, D. Pushin, and H. R. Ott Laboratorium fu¨r Festko¨rperphysik, Eidgeno¨ssische Technische Hochschule–Ho¨nggerberg, 8093 Zu¨rich, Switzerland 共Received 12 January 1999兲 We report the synthesis and characterization of an indium-rich quaternary Yb-Pt-In-Bi compound that is similar to the well-known rare-earth transition-metal stannide Remeika-phase compounds. In addition to structural/composition studies identifying the compound as Yb 5 Pt 6 In 16 Bi 2 , we have made dc and ac magnetic susceptibility, specific heat, resistivity, magnetoresistance, Hall effect, and thermoelectric power measurements on this material. It appears that this Remeika-phase compound 共structure type Tb 5 Rh 6 Sn 18 ) is moderately disordered. Crystal-field effects influence the temperature dependence of the dc magnetic susceptibility, the specific heat, the resistivity, and the thermoelectric power. A cusp in the ac magnetic susceptibility peaks near 300 mK, close in temperature to where the specific heat divided by temperature C p (T)/T also reaches a maximum. The susceptibility feature is frequency dependent and suggestive of a disorder-induced spin-glass transition rather than conventional magnetic order. 关S0163-1829共99兲03830-8兴 INTRODUCTION Since being discovered in the early 1980s, 1–3 Remeika- phase compounds 共tin-rich rare-earth transition-metal stan- nides兲 have attracted much attention, especially because of the coexistence of magnetism and superconductivity that is observed in some members of this family of compounds. 4 Although distorted versions of each exist, 5,6 the materials can be divided into two groups. The first are those derived from a face-centered-cubic structure with lattice constant a ⬇9.7 A, such as R 3 M 4 Sn 13 , often written SrR 3 M 4 Sn 12 be- cause of the multiplicity of Sn sites, where R is a rare earth and M is a transition-metal element. The more complicated group are those derived from a face-centered-cubic structure or with a⬇13.7 A, for example R 5 M 6 Sn 18 Sn 1⫺x R x R 4 M 6 Sn 18 . Both classes of compounds form with many different rare earths and transition metals. 4 We have found that it is also possible to synthesize indium-rich com- pounds in the same structure that seem to share many of the physical properties of these stannides. Here, we report the observation of the larger-cell structure in an Yb-Pt-In-Bi quaternary phase. We also have observed the smaller-cell phase in rare earth-platinum-indium ternaries. 7 The only pre- viously reported group of such compounds that do not con- tain Sn are the rare-earth transition-metal germanides, dis- cussed by Braun. 8 SYNTHESIS AND STRUCTURAL CHARACTERIZATION In an attempt to grow single crystals of Yb-Bi-Pt phases from an indium flux, 9 we have grown single crystals of a quaternary phase Yb-Pt-In-Bi compound. The crystals grow from an approximately 10 molar % solution of the composi- tion YbBiPt in excess In. The synthesis is made in alumina crucibles encapsulated in evacuated silica, by slow cooling from 1100 °C. Multi-faceted crystals with faces up to 1 cm in PRB 60 lateral dimension grow from these melts. They have an ap- pearance and morphology very similar to what is found in the growth of the Remeika stannides from excess Sn. The crystals are clearly quaternary phases as it is not possible to synthesize the material from melts that exclude any of the constituent elements 共in particular Bi兲. Furthermore, it has not proved possible to synthesize the Yb-Pt-In analogue of the 9.7-A fcc stannide, although such a phase can be pro- duced with light rare earths, for example Ce 3 Pt 4 In 13 . 7 The symmetry of the Yb-Pt-In-Bi crystals was established from precession photographs using Mo K ␣ radiation. The photographs display Laue symmetry m3m and reflection conditions hkl: h⫹k,h⫹l,k⫹l⫽2n, 0kl: k,l⫽2n, hhl: h ⫹l⫽2n, h00: h⫽2n, consistent with the space groups F432, F-43m, and Fm-3m. The F cell parameter, deter- mined from the precession photographs, is a⬇13.8 A. Crushed crystals also were examined by powder x-ray dif- fraction, using a Siemens diffractometer and Cu K ␣ radiation, in order to determine accurately the cell constant. The final lattice constant, refined by the least squares method using the absolute angle of 12 high angle reflections, was a Quantitative x-ray microanalysis was performed by apply- ing the Cliff-Lorimer ratio technique 10 to data obtained with a Phillips CM 300 transmission electron microscope 共TEM兲 operating at 300 kV and equipped with a Kevex x-ray energy-dispersive 共XEDS兲 analysis system. The Cliff- Lorimer 共or sensitivity兲 factors, k, used in the XEDS analy- sis, were determined from analysis of the stoichiometric standard compounds YbBiPt and YbInCu 4 . TEM samples of Yb-Pt-In-Bi and of the standard compounds YbBiPt and YbInCu 4 were prepared by crushing single crystals of each compound in anhydrous methanol, dispersing them onto a 1000-mesh TEM grid, and immediately inserting them into the microscope, in order to avoid potential contamination. ‘‘Beam transparent’’ areas along the edges of many crystal- ©1999 The American Physical Society